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Evidence for Photoinduced Insulator-to-Metal transition in B-phase vanadium dioxide

Scientific Reports volume 6, Article number: 25538 (2016) | Download Citation


Ultrafast optical studies have been performed on epitaxial films of the novel B-phase of vanadium dioxide using temperature-dependent optical pump-probe technique. Signature of temperature-driven metal-to-insulator transition was distinctly observed in the ultrafast dynamics — the insulating phase showed two characteristic electronic relaxation times while the metallic phase showed only one. Beyond a threshold value of the pump fluence, the insulating state collapses into a ‘metallic-like’ phase which can be further subdivided into two regimes according to the lengths of the fast characteristic time. The first regime can be explained by lattice heating due to the optical pump; the other cannot be accounted by simple lattice heating effects alone, and thus offers evidence for a true photoinduced phase transition.


Complex oxides provide a variety of materials platform for studying metal-insulator transitions (MIT)1,2. From a technological point of view, there are two crucial issues in MIT transitions — the ability to manipulate, and determining the speed of such transitions. Ultrafast optical measurements have been proven to be highly reliable in understanding the timescale and role of photoexcitation in these phase transitions3. The study of time-dependent carrier dynamics has helped in understanding the contributions of charge, spin, and lattice degrees of freedom to phase transitions in complex oxides4,5,6,7. Recent efforts on time-resolved optical measurements have significantly advanced efforts on optical control of MIT in complex oxides, and have gained a lot of interest particularly owing to its promise of realizing ultra high-speed opto-electronic devices4,8. In the past, several successful attempts to tune the conductivity by light irradiation were observed in manganites, KMoO3, NdNiO3, magnetites, etc.9,10,11,12,13,14. Furthermore, it has also been found that photodoping causes the destruction of charge and orbital order leading to modification of magnetic and electronic phases3,15,16,17,18.

Vanadium dioxide is a complex oxide rich in polymorphism displaying several crystal symmetries that could be stabilized depending on the synthesis conditions19. The most popular and extensively studied polymorph of vanadium dioxide, VO2(M), undergoes a temperature-driven MIT at ~340 K with a concomitant transition in crystal structure2. VO2(B) is also another important polymorph with a rich electronic phase diagram that exhibits a broad insulator to semi-metal transition displaying four orders of resistivity increase as the temperature is lowered from 300 K to 150 K20,21. The schematic energy band diagrams of VO2(B) near the Fermi level depicting the metallic and the insulating phases are shown in Fig. 1(a). Similar to VO2(M), the energy band picture in insulating state of VO2(B) can be described by the separation of the bonding d|| band below the Fermi level EF and π* orbitals above EF. In the insulating phase, a band gap of ~0.6 eV opens up22. Hard X-ray photoelectron spectroscopy (HAXPES) of VO2(B) seem to suggest a larger d|| band splitting in the insulating state of VO2(B), as compared to VO2(M), and the π* band also shifts to higher energy with respect to the with respect to d|| band23. X-ray photoelectron spectroscopy study reveals that VO2(B) is metallic at room temperature, unlike VO2(M) which has an optical band gap of 0.32 eV23. Structurally, VO2(B) adopts a monoclinic crystal structure C2/m(#12) with lattice parameters a = 1.203 nm, b = 0.3693 nm, c = 0.642 nm and β = 106.6° with no temperature-dependent structural phase transition24,25. VO2(B) can be considered as a layered structure composed of two identical atomic layers, the second layer being shifted by with respect to the first one25. VO2(B) with its deformed VO6 octahedra is metastable in nature compared to the rutile phase of VO2.

Figure 1
Figure 1

(a) Schematic diagram of the VO2(B) band structure shown along with the Fermi level at the metallic phase (300 K) and the insulating phase (100 K). (b) Temperature-dependent time evolution of transient reflectivity ΔR/R spectra for VO2(B) films after photoexcitation by a laser fluence of ~1.15 mJ/cm2. Semi-log plot of relative reflectivity fitted with the bi-exponential model for a pump fluence of ~1.15 mJ/cm2 at temperatures — (c) 100 K and (d) 300 K. The arrows represent the delay where the transient reflectivity attains its maximum value, tP.

While there have been a number of reports on the ultrafast phase transition in VO2(M) with the pump laser acting as the driving mechanism for non-thermal phase transitions26,27,28,29,30,31,32,33,34,35, no time-resolved study on VO2(B) has been reported yet. Here, we demonstrate that ultrafast spectroscopy can be utilized to identify the electronic phase transition in VO2(B). We also establish for the first time in VO2(B) that beyond some critical, optical pump fluence threshold Fth, the low-temperature insulating state melts into a ‘metallic-like’ state. Fth is strongly temperature-dependent and there are subtle differences between a light-activated and a thermal-activated phase transition. Single-color pump-probe measurements have been performed in the past to determine the nature of the phase transition in VO2(M), in terms of both electronic property and atomic structural arrangement30.


Time-resolved photoinduced change in reflectivity (or transient reflectivity, ΔR/R) for all measurements were taken up to 1400 picoseconds (ps). Figure 1(b) shows ΔR/R of VO2(B) on SiSTO (Si substrate with SrTiO3 as buffer layer) substrate for temperatures between 100 K and 300 K up to 25 ps, for a pump fluence of 1.15 mJ/cm2. Between 100 K to 160 K, after an initial positive rise of ΔR/R, we see an exponential decrease. On the other hand, for T ≥ 180 K, ΔR/R follows a noticeably different trend — after an initial increase, it does not decrease but instead continues to increase, albeit at a slower rate up to several ps, and eventually decreases gradually. These contrasting behaviors in ΔR/R for T ≤ 160 K and T ≥ 180 K may suggest the presence of different electronic orders in VO2(B), which can be better understood by fitting ΔR/R to an exponential model below.

At a particular temperature, the electronic dynamics of VO2(B) was fitted to a bi-exponential model described as

where A (τ1) and B (τ2) represent the amplitudes (relaxation times) of the fast and slow relaxation processes, respectively, while C represents the extremely long-lived component. Representative fittings at temperatures 100 K and 300 K are shown in Fig. 1(c,d) respectively — notice that at 100 K ΔR/R relaxes immediately after the initial rise after photoexcitation (“relaxation-like”), while at 300 K ΔR/R continues to rise after the initial rise (“growth-like”), till ~10 ps before it finally relaxes. The presence of the slow component, τ2 (300–4000 ps), found in all our measurements, is related to the recovery dynamics. This is consistent with previous time-resolved optical measurements on 50-nm VO2(M) films, which showed that the characteristic time for recovery from the photoexcited metallic to the insulating phase is ~10 ns36. Assuming the recovery dynamics are quite similar, we can expect the photoexcited metallic VO2(B) to relax into the insulating state before the arrival of the next pump pulse. Also shown in Fig. 1(c,d) is tP — defined as the time delay where ΔR/R reaches a maximum immediately following optical excitation.

The black data points in Fig. 2(a–c) show the temperature dependence of A, tP, and τ1, respectively, for a 1.15 mJ/cm2 pump fluence. Figure 2(a) clearly shows that A changes sign at ~170 K, from positive below 170 K to negative at or above 170 K. Comparing this with temperature-dependent transport and optical conductivity studies on VO2(B)20,23, we conclude that the positive A corresponds to the insulating state of VO2(B), while negative A corresponds to the metallic state. Figure 2(b) shows that ~180 K also corresponds to the temperature where tP abruptly increases from sub-ps (in the low-temperature insulating state) to ≥10 ps (in the high-temperature metallic state). Figure 2(c) shows that the fast relaxation time τ1 is significantly lengthened (to ~30 ps) in the vicinity of 180 K. Note also that τ1 in the insulating state of VO2(B), which falls in the range of 1.1–2.8 ps, is comparable to the corresponding values of VO2(M) determined from transient spectroscopy experiments27,30.

Figure 2
Figure 2

Values of A, tP and τ1 for VO2(B) film as a function of (a–c). Temperature, and (d–f ). Fluence. A and τ1 were determined from the bi-exponential fitting results, and tP represents the time delay at the maximum value of ΔR/R. The solid black lines in (a,d) are references for A = 0. The value of Fth at 150 K is indicated by the black arrow in (d).

We repeat the measurements at higher excitation fluences. Figure 3(a,b) shows the time dependence of ΔR/R at various temperatures for excitation densities 1.8 mJ/cm2 and 3.45 mJ/cm2 respectively. For 1.8 mJ/cm2 pump fluence, the dynamics goes from “relaxation-like” at low temperatures, to “growth-like” at high temperatures — similar to what we see for 1.15 mJ/cm2. However, for a 3.45 mJ/cm2 pump fluence, we observed “growth-like” dynamics for all temperatures within 25 ps of pump-probe delay.

Figure 3
Figure 3

Transient reflectivity at various temperature points for pump fluences (a) ~1.8 mJ/cm2 and (b) ~3.45 mJ/cm2 for VO2(B) thin film. (c,d) Shows fluence-dependent transient reflectivity at fixed temperatures 150 K and 300 K respectively.

We now focus on the fluence-dependent ΔR/R at a fixed temperature. Figure 3(c) shows ΔR/R measured at 150 K with pump fluences ranging from 0.46 to 4.6 mJ/cm2. The sharp initial positive peak of ΔR/R was observed for fluences of 0.46 mJ/cm2 and 1.15 mJ/cm2. At higher fluences, the dynamics became growth-like immediately after the arrival of the pump pulse. Figure 3(d) shows fluence-dependent ΔR/R at 300 K. At this temperature, “growth-like” dynamics was observed for all fluences, which is expected as VO2(B) is already deep into the metallic phase.

The three sets of data in each of Fig. 2(a–c) show the temperature dependence of A, tP, and τ1, for pump fluences of 1.15, 1.8 and 3.45 mJ/cm2 pump fluence. For pump fluences of 1.15 and 1.8 mJ/cm2 we see a similar trend — (1) the coefficient A going from positive in the low-temperature insulating phase, to negative in the high-temperature metallic phase, changing sign at ~170 K (at 1.15 mJ/cm2 pump fluence) and ~140 K (at 1.8 mJ/cm2 pump fluence), and (2) tP abruptly increasing from sub-ps to ~10 ps at ~170 K (at 1.15 mJ/cm2 pump fluence) and ~140 K (at 1.8 mJ/cm2 pump fluence), and (3) τ1 exhibiting a broad peak near ~170 K (at 1.15 mJ/cm2 pump fluence) and ~140 K (at 1.8 mJ/cm2 pump fluence). On the other hand, for all temperatures at a pump fluence of 3.45 mJ/cm2, the coefficient A remains negative. The change in A from positive to negative, and the concomitant lengthening of τ1, could signify the melting of the insulating order in VO2(B), which we will discuss later in the context of photoinduced phase transition.

Figure 2(d–f) show the fluence-dependent plots of A, tP, and τ1 at a fixed temperature, and shows similar trends to the temperature-dependent plots. As the pump fluence is systematically increased while keeping the temperature constant at 150 K, ΔR/R changed from “relaxation-like” to “growth-like” at a “threshold” fluence, Fth, of 1.5 mJ/cm2, as shown by the change of sign of A from positive to negative. There is also a concomitant lengthening of τ1 at the same value of Fth. Also note that, as temperature is increased, Fth becomes lower — this behaviour is seen in both the temperature and fluence-dependent data. The value of Fth differs significantly between VO2(M) and VO2(B) — at room temperature, VO2(M) is completely insulating and requires Fth of 6‒7 mJ/cm2 but if we chose 150 K as the analogous temperature in VO2(B), the required Fth is only 1.5 mJ/cm231.

The photoinduced MIT transition is illustrated by mapping the phase diagram of VO2(B) in non-equilibrium conditions [Fig. 4]. The phase boundaries are estimated from the values of Fth determined from fluence-dependent and temperature-dependent data (eg. Fth at 150 K is 1.5 mJ/cm2) where the coefficient A crosses from positive to negative. The metallic state is further subdivided into two regimes — I and II to represent the slow growth and the fast growth dynamics respectively. When in the photoinduced metallic state of VO2(B), we designate as regime I when τ1 > 3 ps, and regime II when τ1 ≤ 3 ps. This separation of regimes I and II is based on our data which indicates that for a fluence of 3.45 mJ/cm2, the system is in regime II and at this fluence, τ1 ≤ 3 ps.

Figure 4: Summary of the dynamics study of VO2(B) as represented by the phase diagram.
Figure 4

The red and the blue shaded regions represent the metallic state and the insulating states respectively. The metallic phase is further subdivided into two regions — (I) thermally induced exhibiting longer τ1 (light blue and red streaks) and (II) photoinduced (coloured red) where τ1 ≤ 3 ps.

We now discuss the physical origins of the different components. The fast relaxation time, τ1 in the insulating state of VO2(B) could arise from self-trapping of photoexcited carriers similar to the observations in VO2(M)26,28,37. On the other hand, the origin of τ1 in the ‘metallic-like’ state of VO2(B) is difficult to interpret. In the transition region going from the insulating to metallic state, whether as a function of temperature or fluence, excited carriers may be temporally trapped in metastable, transient energy states leading to a large τ1. The increase of relaxation time with increasing pump fluence has also been reported in systems like intercalated bilayer graphene — there the increase in the electron-phonon relaxation time was explained using the reabsorption of optical phonons by the carriers leading to a quasi-equilibrium state which slows the rate of hot electron cooling38.

In VO2(M), the growth dynamics in the photoinduced metallic phase is interpreted as a result of seeding of metallic nano-domains by light which eventually expands outwards into the insulating regions via dynamical and percolating growth28,35. A complete phase transition of photoexcited VO2(M) may take as long as 100 ps; beyond that, photoexcitation merely increases the film temperature29,35,39. The time scale of the growth dynamics in VO2(B), in regime I, falls in this range. Lattice heating due to the pump laser can account for the energy required to cross into metallic regime I, and in this scenario nucleation and growth of metallic phases are possible. However the laser energy is not sufficient for the system to reach metallic regime II. One can estimate the upper limit of increase in lattice temperature by considering that the entire pump energy has been converted to absorbed heat. The corresponding temperature change for fluence as large as 3.45 mJ/cm2 is only 32.5 K compared to the large transition width of 150 K (Supplementary information). This means that the pure lattice heating effects can drive the insulating state of VO2(B) to regime I in the phase diagram but not into regime II.

Further calculations at each of the temperature points show that the temperature rise, ΔT due to lattice heating is inversely proportional to the initial system temperature (Supplementary information). In Fig. 4, the width of regime I decreases with increasing temperature. This shape of the phase boundary in regime I agree with our calculations.

The photoinduced metallic phase in regime II can be understood by estimating the carrier density in the system. Assuming that one pump photon creates one free charge carrier, the density of the photogenerated carriers, Δn can be estimated using the relation where R = 0.11 is the reflectivity of light (800 nm) in the low-temperature insulating state, v is the corresponding frequency for a wavelength of 800 nm, and absorption coefficient α = 5.5 × 104 cm−1 for VO2(B) film as obtained from the absorbance spectrum (Supplementary Information). At a pump fluence of 3.45 mJ/cm2, Δn ~ 3.1 × 1021 cm−3. It is important to mention here that this value of photogenerated carrier density in VO2(B) is comparable to the free-carrier density in metallic VO2(B) (~1022 cm−3) obtained from Hall experiments at 300 K23. At such a large free-carrier concentration, the system cannot remain insulating until the system completely relaxes. This is six orders of magnitude larger than the carrier density in the insulating phase23.


In summary, the photoinduced effect on the various electronic phases of VO2(B) has been studied for the first time by ultrafast pump-probe technique. Transient reflectivity (ΔR/R) dynamics demonstrate that the insulating state has an initial sharp peak and decays within a few ps. The metallic state induced by lattice heating from the pump laser has a slower growth of ΔR/R and survives for a longer time becoming as long as several tens of ps. Finally, we discuss the possibility of a pure photoinduced phase transition in the regime which cannot be accounted by simple lattice heating. Our results should guide future time-resolved multi-color experiments on this system. Experiments at lower repetition rates will help to disentangle the lattice heating effects with that of a pure photoinduced phase transition.


Sample growth

50-nm VO2(B) thin films were fabricated by Pulsed Laser Deposition by ablating a commercial vanadium metallic target. The substrate chosen was specially fabricated Si with a buffer layer of 20 nm SrTiO3 (SiSTO). The growth of B-phase VO2 thin films was stabilized at a temperature of 500 °C and a fixed laser energy density of 2 J/cm2 and the oxygen pressure was kept between 5 × 10−3 to 7 × 10−3 Torr. The thickness of VO2(B) thin film used for the pump-probe study was ~50 nm. The detailed growth study has been discussed in an earlier publication23.


The transient reflectivity measurements in our pump-probe experiments were performed using a Ti:sapphire regenerative amplifier system (Coherent RegA with a repetition rate of 250 kHz). Sub-50 fs pulses at a center wavelength of 800 nm generated by the laser was used as a source of both pump and probe pulses. The pump and probe pulses were cross polarized. The beam diameter of the pump was set to ~50 μm while the probe beam was focused to a smaller diameter of 25 μm which ensured an excellent pump-probe overlap. The reflected probe beam was focused onto a photodiode detector which was connected to a lock-in amplifier where the photoinduced changes in reflectivity ΔR/R were recorded. Temperature and fluence dependent measurements were taken on the sample which was mounted on a continuous flow cryostat. For fluence dependent measurements, the probe power was kept constant while the pump power was steadily increased without any other changes in the beam parameters.


We performed absorbance spectrum measurements in the range 220‒900 nm with the help of commercial UV-Vis spectrophotometer (Jasco, Model V-650).

Additional Information

How to cite this article: Lourembam, J. et al. Evidence for Photoinduced Insulator-to-Metal transition in B-phase vanadium dioxide. Sci. Rep. 6, 25538; doi: 10.1038/srep25538 (2016).


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We thank the NUSNNI-NanoCore at the National University of Singapore, Singapore and National Research Foundation (NRF), Singapore, under the Competitive Research Program (CRP) “Tailoring Oxide Electronics by Atomic Control” NRF2008NRF-CRP002-024, CRP “Interface Science and Technology” NRF-CRP4-2008-04, National University of Singapore (NUS) cross-faculty grant and FRC (ARF Grant No. R-144-000- 278-112), and MOE Tier 1 RG123/14 for the financial support. We also acknowledge the funding support from the Singapore NRF through the Singapore-Berkeley Research Initiative for Sustainable Energy (SinBeRISE) CREATE Programme. C.L. acknowledges the support from the Theoretical and Computational Science (TaCS) Center (TaCS 2559-9).

Author information

Author notes

    • James Lourembam

    Present address: Data Storage Institute, 2 Fusionopolis Way, Singapore 138634, Singapore.


  1. Division of Physics and Applied Physics, School of Physical and Mathematical Sciences, Nanyang Technological University, Singapore 637371, Singapore

    • James Lourembam
    • , Liang Cheng
    •  & Elbert E. M. Chia
  2. NUSNNI-Nanocore, National University of Singapore, Singapore 117411, Singapore

    • Amar Srivastava
    •  & T. Venkatesan
  3. Department of Physics, National University of Singapore, Singapore 117542, Singapore

    • Amar Srivastava
    •  & T. Venkatesan
  4. Nanoscience and Nanotechnology Graduate Program, King Mongkut’s University of Technology Thonburi (KMUTT), 10140, Thailand

    • Chan La-o-vorakiat
  5. Faculty of Science, King Mongkut’s University of Technology Thonburi (KMUTT), 10140, Thailand

    • Chan La-o-vorakiat
  6. Theoretical and Computational Science Center (TaCS), Faculty of Science, King Mongkut’s University of Technology Thonburi (KMUTT), 10140, Thailand

    • Chan La-o-vorakiat
  7. Department of Electrical and Computer Engineering, National University of Singapore, Singapore 117576, Singapore

    • T. Venkatesan
  8. Department of Materials Sciences and Engineering, National University of Singapore, Singapore 117576, Singapore

    • T. Venkatesan
  9. Department of Integrated Sciences and Engineering, National University of Singapore, Singapore 117456, Singapore

    • T. Venkatesan


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J.L., T.V. and E.E.M.C. designed the research. A.S. fabricated the thin films. J.L. performed the OPOP measurements with assistance from L.C., C.L. and J.L. conducted the experiments on UV-Vis spectrometer. The data was analyzed by J.L. and E.E.M.C. The manuscript was prepared by J.L. with assistance from E.E.M.C., T.V., C.L. and A.S. All the authors contributed to discussion of the results and commented on the manuscript.

Competing interests

The authors declare no competing financial interests.

Corresponding authors

Correspondence to T. Venkatesan or Elbert E. M. Chia.

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